Beta-quartz glass-ceramics with a controlled transmission curve and a high iron oxide content; articles comprising said glass-ceramics, and precursor glasses

ABSTRACT

β-quartz lithium aluminosilicate (LAS) glass-ceramics contain neither arsenic oxide nor antimony oxide, are fined with tin oxide and include vanadium oxide, chromium oxide and a high iron oxide content (&gt;950 ppm), and have a controlled transmission curve. Articles such as cook-tops can be made from such glass-ceramics.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims the benefit of priority under 35 U.S.C. §119 of French Patent Application Serial No. 1261122 filed on Nov. 22, 2012, the entire content of which is hereby incorporated by reference.

FIELD

The disclosure relates generally to lithium aluminosilicate (LAS) type glass-ceramics, and more particularly to darkened LAS glass-ceramics having a solid solution of β-quartz as the predominant crystalline phase. Also disclosed are articles formed from such glass-ceramics, precursor glasses of such glass-ceramics, and methods for obtaining such glass-ceramics and articles.

BACKGROUND

The disclosure relates to the field of β-quartz glass-ceramics. More particularly it relates to tin-fined, darkened glass-ceramics of the lithium aluminosilicate type, containing a solid solution of β-quartz as the main crystalline phase, essentially free of As₂O₃ and of Sb₂O₃, articles comprising said glass-ceramics, and lithium aluminosilicate glasses as precursors of such glass-ceramics, as well as methods for forming said glass-ceramics and said articles.

With view to the toxicity of As₂O₃ and of increasingly strict regulations in effect, this toxic fining compound is desirably no longer used. For environmental considerations, it is also desired to no longer use Sb₂O₃ and not to use halogens, such as F and Br, which would have been able to replace at least partly said fining agents As₂O₃ and Sb₂O₃.

SnO₂ has been proposed as a replacement fining agent. It is notably used when the precursor glass of the glass-ceramic (glass plate precursors of glass-ceramic plates, in fact) is obtained by floating. Indeed, applied with glasses containing As₂O₃ and/or Sb₂O₃ in their composition, such a floating method generates glass plates with a metal deposit at their surface (a metal deposit resulting from the reduction of As₂O₃ and/or Sb₂O₃).

The use of SnO₂ as a fining agent however has two major drawbacks. It is less efficient than As₂O₃ (and, in absolute terms, it should therefore be used in a relatively large amount, which is not without posing any problems, more particularly of devitrification) and, as a more powerful reducing agent than As₂O₃ and Sb₂O₃, it is responsible for the appearance of an undesirable yellowish coloration during ceramming. This second drawback is of course a nuisance when it is sought to obtain transparent, essentially colorless glass-ceramics. This yellowish coloration results from Sn—Fe, Sn—Ti and Ti—Fe interactions, i.e., by way of charge transfer.

In view of the foregoing, it would be advantageous to provide colored glass-ceramic compositions that are substantially free of As₂O₃ and Sb₂O₃, and which possess desired optical properties particularly for their use in stove cook-tops.

BRIEF SUMMARY

A glass-ceramic of the lithium aluminosilicate (LAS) type contains a β-quartz solid solution as the predominant crystalline phase and, for a thickness of 4 mm, has an integrated optical transmission, T_(v), in the visible range, of 0.8 to 2%, an optical transmission at 625 nm of more than 3.5%, an optical transmission at 950 nm between 40 and 70%, and an optical transmission at 1,600 nm between 50 and 75%.

The LAS composition, expressed as percentages by weight of oxides, comprises 0.2 to less than 0.3% SnO₂, 0.025 to 0.2% V₂O₅, 0.01 to 0.04% Cr₂O₃, greater than 0.095 to 0.32% Fe₂O₃, and less than 0.1% As₂O₃+Sb₂O₃. A ratio Fe₂O₃/V₂O₅ of the iron oxide and vanadium oxide content is from 1 to 4.

Additional features and advantages of the subject matter of the present disclosure will be set forth in the detailed description which follows, and in part will be readily apparent to those skilled in the art from that description or recognized by practicing the subject matter of the present disclosure as described herein, including the detailed description which follows as well as the claims.

It is to be understood that both the foregoing general description and the following detailed description present embodiments of the subject matter of the present disclosure, and are intended to provide an overview or framework for understanding the nature and character of the subject matter of the present disclosure as it is claimed. Additionally, the descriptions are meant to be merely illustrative, and are not intended to limit the scope of the claims in any manner.

BRIEF DESCRIPTION OF THE DRAWINGS

The FIGURE shows the optical transmission spectrum of a glass-ceramic plate according to Example 1.

DETAILED DESCRIPTION

Glass-ceramics colored with vanadium oxide (V₂O₅) can have a coefficient of thermal expansion close to zero in order to withstand thermal shock. For use as cooktops, they may possess a specific suite of optical transmission properties. In embodiments, the optical transmission curves for a 4 mm thick plate of the glass-ceramic include an integrated optical transmission T_(V), in the visible range (i.e., between 380 and 780 nm) measured with the illuminant D65 with an angle of 2° to the observer of 0.8 to 2% (e.g., 1 to 1.7%). If the integrated optical transmission is greater than 2%, heating elements located under the plate will not be properly concealed when the cooktop is not in operation. If the integrated optical transmission is less than 0.8%, the heating elements will not be suitable visible during operation, which may pose a safety hazard.

In addition to the integrated transmission, the optical transmission at 625 nm (T₆₂₅) in embodiments is greater than 3.5% (e.g., greater than 4%). With this, it is possible to see red displays disposed under the plate. The optical transmission at 950 nm (near infrared), (T₉₅₀) can be between 40 and 70% (e.g., from 50 to 70%). A near-IR transmission greater than or equal to 50% makes it possible to use conventional electronic control buttons, emitting and receiving at these wavelengths. The infrared optical transmission at 1,600 nm (T₁₆₀₀) can be between 50 and 75%. If the infrared optical transmission is less than 50%, the heating performances of the plates are not satisfactory, and if said infrared optical transmission is greater than 75%, the heating performance may be excessive and, for example, induce dangerous heating of materials placed in proximity to the plate.

Boiling point measurement tests (of water) have shown that a transmission at 1,600 nm greater than or equal to 50% is sufficient to provide a satisfactory boiling time.

Boiling point tests were carried out by placing the glass-ceramic to be tested on a hotplate with a diameter of 145 mm. Two tests were carried out by calibrating the hotplate so that the maximum surface temperature of the glass-ceramic was 560° C. or 620° C. In each case, the time required to raise the temperature of a liter of water from 20 to 98° C. was measured. The water was placed in a pot covered with aluminum of the same diameter as the hotplate. Two comparative glass-ceramics were tested: Kerablack® glass-ceramic with a transmission of 67.9% at 1,600 nm and a glass-ceramic called “Glass-ceramic T” with a transmission of 54.9% at 1,600 nm. Results of the two materials are not significantly different (to be considered significantly different, the difference between two boiling times must exceed 30 s).

TABLE 1 Boiling point data for comparative glass-ceramic plates Glass-ceramic “T” Kerablack ® Glass-Ceramic Transmission at 1,600 nm 54.9% 67.9% Maximum surface temperature 560° C. 620° C. 560° C. 620° C. Boiling time Test 1 7′ 14″ 6′ 27″ 6′ 40″ 6′ 29″ Test 2 9′ 26″ 7′ 29″ 9′ 26″ 7′ 31″

While the boiling point data are satisfactory, each of the comparative compositions contains arsenic oxide as a fining agent. During the successive glass-ceramic formation steps of melting and fining of a vitrifiable load of raw materials, shaping, and crystallization (i.e., ceramming), the avoidance of arsenic oxide (and antimony oxide) as fining agents is desirable.

In various embodiments, glass-ceramics are disclosed having comparable optical transmission properties to Kerablack® glass-ceramic plates, but without the inclusion of arsenic oxide or antimony oxide in the composition.

Example glass-ceramic compositions include Fe₂O₃ and relatively low SnO₂ content. Relatively high Fe₂O₃ content enables the use of starting materials that are less pure and thus less expensive, including a greater quantity of recycled materials (cullet). However, it is believed that the addition of iron oxide has an impact on the optical qualities of the product obtained, in terms of transmission in the visible as well as in the infrared.

Meanwhile, SnO₂ is an expensive raw material. Therefore, a relatively low content of tin oxide makes it possible to limit the raw material cost as well as minimize adverse effects associated with the condensation of tin metal within the furnace.

In such a context, disclosed are glass-ceramic compositions that are free of arsenic (and of antimony) or containing only traces thereof, including tin oxide and a high iron oxide content, and having an optimized optical transmission curve in the visible and infrared ranges. Such glass ceramics can be fined at conventional fining temperatures, generally between 1,600 and 1,700° C.

The disclosed compositions include relatively low proportions of SnO₂ (which provides a fining agent function and a reducing agent function, where the reducing agent participates in the final coloration of the product), high proportions of Fe₂O₃, and one or more of V₂O₅ and Cr₂O₃ as coloring species.

In embodiments, the disclosed glass-ceramics are lithium aluminosilicate (LAS) type glass-ceramics containing Li₂O, Al₂O₃ and SiO₂ as essential constituents of the β-quartz solid solution, where a β-quartz solid solution is the predominant crystalline phase accounting for more than 80% by weight of the total crystalline phase of the crystallized fraction.

The disclosed glass-ceramics exhibit optical transmission characteristics, for a thickness of 4 mm of: 0.8%≦T_(V)≦2%, for example, 1%≦T_(V)≦1.7%, T₆₂₅>3.5%, for example, T₆₂₅>4%, 40%≦T₉₅≦70%, for example, 50%≦T₉₅≦70%, and 50%≦T₁₆₀≦75%.

In further embodiments, the composition of the glass-ceramics, expressed as percentages by weight of oxides, includes SnO₂: 0.2 to <0.3%, for example 0.23 to 0.29%, V₂O₅: 0.025 to 0.2%, for example, 0.05 to 0.2%, Cr₂O₃: 0.01 to 0.04%, Fe₂O₃: >0.095 to 0.32%, As₂O₃+Sb₂O₃: <0.1%, and a ratio Fe₂O₃/V₂O₅ of 1 to 4, for example 1 to 2. In contrast, Kerablack® glass-ceramics contain roughly 700 ppm of Fe₂O₃.

The glass-ceramics have a dark color and are suitable for use, for example, as cooktops.

The glass-ceramics contain neither any As₂O₃, nor any Sb₂O₃ or only contain traces of at least one of these compounds, SnO₂ being present instead of and in place of these conventional fining agents. If traces of at least one of these compounds are present, this is as a contaminating product, which is likely due to the presence of recycled materials in the vitrifiable load of raw materials. In any case, only traces of these toxic compounds are likely to be present: As₂O₃+Sb₂O₃<1,000 ppm.

The compositions include tin oxide. The content of tin oxide can be controlled to achieve the desired fining while avoiding devitrification or adverse effects on the color package. Notably, SnO₂ is capable of reducing vanadium and the iron present during ceramming. In embodiments, the SnO₂ content ranges from 0.2 to <0.3 wt. %, for example 0.23 to 0.29%, 0.24% to 0.29%, 0.25 to 0.28%, or 0.25 to 0.27%. The measurement uncertainty for the SnO₂ content is +/−50 ppm (+/−0.005%).

Vanadium oxide is used as a coloring agent. Indeed, V₂O₅ in the presence of SnO₂ may significantly darken the glass during its ceramming V₂O₅ is responsible for absorption mainly below 700 nm and it is possible in its presence to retain sufficiently high transmission in the infrared. An amount of V₂O₅ between 0.025-0.2% (i.e., between 250 and 2,000 ppm) may be used. In embodiments, the V₂O₅ content is between 0.03 and 0.2%, such as between 0.05 and 0.2%, between 0.06 and 0.2%, i.e., >0.06-0.2%, or between 0.07 and 0.2%.

It is challenging in a glass-ceramic comprising both SnO₂ and V₂O₅ to obtain the sought after integrated optical transmission (T_(v)) and the required optical transmission at 625 nm (T₆₂₅). Indeed, insofar that the absorption due to vanadium is relatively high at this wavelength (625 nm), when an acceptable value is reached for the integrated optical transmission, the value of the optical transmission at 625 nm may be too low and vice versa.

Applicants have solved the challenge by combining chromium oxide with vanadium oxide to create a coloring package (comprising V₂O₅, Cr₂O₃ and Fe₂O₃) capable of providing the desired optical properties.

Chromium oxide (Cr₂O₃) can be used as a darkening agent in the visible range (400-600 nm) while retaining high transmission in the wavelengths between 600 and 800 nm. The amount of Cr₂O₃ may range from 0.01 to 0.04% by weight. For instance, the Cr₂O₃ content may range from >0.015-0.04%, e.g., >0.015-0.035% or 0.016-0.035%.

The glass-ceramics thus exhibit very low transmission in the blue range. For a thickness of 4 mm, the disclosed glass-ceramics generally have an optical transmission at 450 nm of less than 0.1% (T₄₅₀<0.1%), and/or an optical transmission at 465 nm of less than 0.1% (T₄₆₅<0.1%).

Iron oxide promotes absorption mainly in the infrared. In order to make efficient use of recycled products and low-cost starting materials, the Fe₂O₃ content may be greater than 950 ppm, e.g., at least 1,000 ppm. If the Fe₂O₃ content exceeds 3,200 ppm, however, absorption in the infrared may be too high. Such a high Fe₂O₃ content may also complicate the melting and fining processes. In example glass-ceramics, the iron oxide content is between 1,000 and 3,000 ppm, e.g., between 1,200 and 2,900 ppm, or between 1,500 and 2,900 ppm. It was surprisingly observed that a transmission at 1,600 nm greater than 50% could be obtained with iron oxide contents up to 3,200 ppm. Further, iron oxide content in the range of 950 to 3200 ppm promotes fining in combination with a relatively low amount of tin oxide. The combination of a relatively low SnO₂ content and high iron oxide content is thus particularly relevant both to decreasing costs and to maintaining proper fining capacities. The measurement uncertainty for the Fe₂O₃ content is +/−50 ppm (+/−0.005%).

In the visible range, iron is also involved in the coloration process. Its effect within the disclosed compositions may be compensated by that of the vanadium. It was observed that for an Fe₂O₃ content between 900 and 3,200 ppm, transmission in the visible range increased with increasing iron content. It is believed that over this range of iron content, tin oxide preferentially reduces Fe₂O₃ rather than V₂O₅. Such lightening of the glass-ceramic may then be compensated by controlling the V₂O₅ content. Thus, in embodiments, the Fe₂O₃/(V₂O₅) ratio ranges from 1 to 4, e.g., 1 to 2 or 1.3 to 1.8.

In addition to V₂O₅, Cr₂O₃ and Fe₂O₃, other coloring agent such as CoO, MnO₂, NiO, CeO₂ may be included. In order to avoid significantly modifying the optical transmission curve, such additional colorants may be limited. CoO, for example, may be present in a very small amount insofar that it strongly absorbs in the infrared and at 625 nm. The disclosed glass-ceramics may include less than 200 ppm, e.g., less than 100 ppm of CoO.

According to further embodiments, the glass-ceramics do not contain any fining auxiliaries such as F and Br, except for inevitable traces. This is particularly advantageous considering the toxicity of these components.

In addition to SnO₂, V₂O₅, Cr₂O₃ and Fe₂O₃ in the weight percentages specified above (with As₂O₃+Sb₂O₃<1,000 ppm), the glass-ceramic compositions may include:

SiO₂ 60-72 Al₂O₃ 18-23 Li₂O 2.5-4.5 MgO 0-3 ZnO 0-3 TiO₂ 1.5-4  ZrO₂  0-2.5 BaO 0-5 SrO 0-5 BaO + SrO 0-5 CaO 0-2 Na₂O  0-1.5 K₂O  0-1.5 P₂O₅ 0-5 B₂O₃  0-2.

According to embodiments, the glass-ceramics may have a composition consisting essentially of at least 98% by weight, e.g., at least 99% by weight, or even 100% by weight of SnO₂, V₂O₅, Cr₂O₃, Fe₂O₃, As₂O₃, Sb₂O₃, SiO₂, Al₂O₃, Li₂O, MgO, ZnO, TiO₂, ZrO₂, BaO, SrO, CaO, Na₂O, K₂O, P₂O₅ and B₂O₃. A corresponding base glass may be less viscous than competitive glasses such as glasses used to form Kerablack® glass-ceramic products. Indeed, the presently disclosed glass ceramics, which may exhibit less darkening during post-ceramming heat treatments, may be suitable alternatives to Kerablack® glass-ceramics.

The disclosed glass-ceramics may have a coefficient of thermal expansion lower than 10×10⁻⁷ K⁻¹ over the range 25° C. to 700° C., e.g., less than 3×10⁻⁷ K⁻¹.

Further embodiments relate to articles comprising the disclosed glass-ceramic compositions. Such articles may consist essentially of or consist of the glass-ceramic. Example articles are cooktops, cooking utensils or microwave oven trays.

Still further embodiments relate to lithium aluminosilicate glasses that are precursors of the glass-ceramics. A precursor glass may have a composition equal to the corresponding glass-ceramic composition.

Methods for forming glass-ceramics and articles comprising the glass-ceramics are also disclosed. Such methods may include heat treating a vitrifiable load of raw materials under conditions which successively ensure melting, fining and then ceramming.

An example method for forming a glass-ceramic article successively comprises melting a load of vitrifiable raw materials, said load containing SnO₂ as a fining agent, fining of the obtained molten glass, cooling the fined molten glass and simultaneously shaping it to a desired shape for the article, and heat treating the shaped glass to transform the glass into a glass-ceramic.

EXAMPLES

Raw materials were combined to form 1 kg batches having the compositions summarized in Table 1. The mixtures were placed in platinum crucibles and melted at 1,650° C. After melting, the glasses were rolled to a thickness of 5 mm and annealed at 650° C. for 1 hr. Glass samples (in the form of plates of about 10 cm×10 cm) undergo a crystallization treatment comprising a fast heating to 650° C., heating from 650° C. to 820° C. at a heating rate of 5° C./min, heating from 820° C. to the maximum crystallization temperature, T_(max)=920° C. at a heating rate of 15° C./min, maintaining T_(max) for 8 minutes, then cooling at the cooling rate of the oven.

The optical properties of the obtained glass-ceramic plates are measured on polished samples with a thickness of 4 mm. The illuminant D65 (observer at 2°) was used. T_(v) is the integrated transmission in the visible range, and T₄₅₀, T₄₆₅, T₆₂₅, T₉₅₀ and T₁₆₀₀ are the transmissions measured at 450, 465, 625, 950 and 1,600 nm respectively.

In Table 1b, the Examples A, B, C, D and E are comparative. Example A is a Kerablack® glass-ceramic, which contains arsenic. Example B has a Fe₂O₃/V₂O₅ ratio of 4.64 and too high a visible transmission. Example C has a V₂O₅ content of 0.255 and too low a visible transmission. In Example D, the Fe₂O₃ content and the V₂O₅ content are each too high and the visible and infrared transmissions are too low. In Example E, the Fe₂O₃/V₂O₅ ratio is too low and the visible transmission is too low.

TABLE 1a Example Glass-Ceramics Examples 1 2 3 4 5 6 7 8 SiO₂ 64.722 64.538 64.448 64.653 64.421 64.801 64.412 64.618 Al₂O₃ 21.05 21.12 21.23 20.96 21.15 20.71 21.02 21.1 Li₂O 3.8 3.8 3.8 3.8 3.8 3.8 3.8 3.8 MgO 0.33 0.34 0.34 0.33 0.34 0.34 0.34 0.34 ZnO 1.41 1.48 1.43 1.42 1.46 1.47 1.45 1.47 BaO 2.47 2.53 2.49 2.49 2.51 2.52 2.5 2.5 TiO₂ 3.06 3.07 3.05 3.05 3.04 3.07 3.07 3.03 ZrO₂ 1.45 1.38 1.37 1.5 1.37 1.4 1.44 1.39 SnO₂ 0.26 0.25 0.27 0.25 0.26 0.26 0.26 0.29 Na₂O 0.57 0.57 0.57 0.57 0.58 0.56 0.58 0.58 K₂O 0.24 0.24 0.24 0.24 0.24 0.25 0.24 0.24 CaO 0.41 0.41 0.42 0.41 0.42 0.43 0.42 0.42 V₂O₅ 0.083 0.091 0.126 0.111 0.153 0.128 0.158 0.073 Fe₂O₃ 0.123 0.158 0.192 0.192 0.232 0.226 0.283 0.125 Cr₂O₃ 0.0205 0.0220 0.0234 0.0228 0.0240 0.0333 0.0263 0.0228 CoO 0.0015 0.0010 0.0006 0.0012 0.0000 0.0017 0.0007 0.0012 Fe₂O₃/V₂O₅ 1.48 1.74 1.52 1.73 1.52 1.77 1.79 1.71 Tv (%) 1.57 1.98 2 1.87 1.86 1.56 1.45 1.38 T 450 (%) 0.01 0.01 0.01 0.01 0 0.00 0 0.01 T 625 (%) 5.14 6.35 6.52 6.17 6.24 5.35 5.13 4.63 T 950 (%) 61.42 58.01 54.4 53.98 50.4 50.05 44.5 60.9 T 1600 (%) 69.86 65.91 62 62.18 58.7 59.76 54.2 69.4

TABLE 1b Comparative Glass-Ceramics Examples A B C D E SiO₂ 64.918 64.710 64.709 64.880 Al₂O₃ 20.79 20.79 20.69 20.72 Li₂O 3.8 3.8 3.8 3.8 MgO 0.33 0.33 0.33 0.33 ZnO 1.4 1.4 1.51 1.53 BaO 2.48 2.48 2.5 2.51 TiO₂ 3.06 3.06 3.01 3.04 ZrO₂ 1.43 1.43 1.35 1.37 SnO₂ 0.25 0.25 0.27 0.26 Na₂O 0.56 0.56 0.56 0.57 K₂O 0.25 0.25 0.26 0.25 CaO 0.43 0.42 0.42 0.43 V₂O₅ 0.05 0.255 0.213 0.18 Fe₂O₃ 0.232 0.232 0.347 0.106 Cr₂O₃ 0.0192 0.0322 0.03 0.0223 CoO 0.0008 0.0008 0.001 0.0017 Fe₂O₃/V₂O₅ 4.64 0.91 1.63 0.59 Tv (%) 0.8-2.0 7.14 0.57 0.6 0.50 T 450 (%) 0.11 0.00 0.00 0.00 T 625 (%) ≧4.0 17.26 2.37 2.44 2.04 T 950 (%) 40-68 57.65 42.67 34.98 54.40 T 1600 (%) 50-75 59.55 57.17 48.10 70.30

Several additional characterizations were carried out on select glass-ceramics and results are presented in Table 2. The coefficient of thermal expansion between 25° C. and 700° C. (CTE_(25-700° C.) (10⁻⁷ K⁻¹)) and an x-ray diffraction analysis were conducted on Examples 5 and 7. The x-ray data were used to calculate the percentage by weight of the beta-quartz phase and the average size of these crystals.

TABLE 2 Example 5 7 CTE_(25-700° C.) (10⁻⁷ K⁻¹) 2.3 % β-quartz 96% Crystal size 39 nm

A melting test was performed with precursor glasses corresponding to Example 9 and comparative Example F. Both glasses, the compositions of which are indicated in Table 3, were melted using an electric furnace pre-heated to 1,400° C. The melting cycle including raising the temperature from 1,400° C. to 1,600° C. within 2 hrs, and maintaining 1,600° C. for 1 hr.

The samples were taken out of the furnace and the molten glass was poured on a heated steel plate. The glass was rolled to a thickness of 5 mm and annealed for 1 hr at 650° C. Because of the short hold time at 1,600° C., the fining is incomplete. The number of bubbles in the glass plates was counted by a camera coupled with an image analyzer. These results are given in Table 3, expressed as the number of bubbles per cm³. The data how that Example 9 is at least as well fined as the comparative glass F.

TABLE 3 Glass Fining Results Examples Composition 9 F SiO₂ 64.678 64.892 Al₂O₃ 20.8 20.8 Li2O 3.8 3.8 MgO 0.35 0.35 ZnO 1.5 1.5 BaO 2.5 2.5 TiO₂ 3 3 ZrO₂ 1.4 1.4 SnO₂ 0.25 0.35 Na₂O 0.6 0.6 K2O 0.25 0.25 CaO 0.4 0.4 V₂O₅ 0.154 0.05 Fe₂O₃ 0.3 0.09 Cr₂O₃ 0.0167 0.0167 CoO 0.0013 0.0013 Fe₂O₃/V₂O₅ 1.2 1.8 Number of bubbles per cm³ 200 380

An optical transmission spectrum of the Example 1 glass-ceramic plate is shown in the FIGURE.

As used herein, the singular forms “a,” “an” and “the” include plural referents unless the context clearly dictates otherwise. Thus, for example, reference to a “vitrifiable raw material” includes examples having two or more such “vitrifiable raw materials” unless the context clearly indicates otherwise.

Ranges can be expressed herein as from “about” one particular value, and/or to “about” another particular value. When such a range is expressed, examples include from the one particular value and/or to the other particular value. Similarly, when values are expressed as approximations, by use of the antecedent “about,” it will be understood that the particular value forms another aspect. It will be further understood that the endpoints of each of the ranges are significant both in relation to the other endpoint, and independently of the other endpoint.

Unless otherwise expressly stated, it is in no way intended that any method set forth herein be construed as requiring that its steps be performed in a specific order. Accordingly, where a method claim does not actually recite an order to be followed by its steps or it is not otherwise specifically stated in the claims or descriptions that the steps are to be limited to a specific order, it is no way intended that any particular order be inferred. Any recited single or multiple feature or aspect in any one claim can be combined or permuted with any other recited feature or aspect in any other claim or claims.

It is also noted that recitations herein refer to a component being “configured” or “adapted to” function in a particular way. In this respect, such a component is “configured” or “adapted to” embody a particular property, or function in a particular manner, where such recitations are structural recitations as opposed to recitations of intended use. More specifically, the references herein to the manner in which a component is “configured” or “adapted to” denotes an existing physical condition of the component and, as such, is to be taken as a definite recitation of the structural characteristics of the component.

While various features, elements or steps of particular embodiments may be disclosed using the transitional phrase “comprising,” it is to be understood that alternative embodiments, including those that may be described using the transitional phrases “consisting” or “consisting essentially of,” are implied. Thus, for example, implied alternative embodiments to a glass-ceramic that comprises a various oxides include embodiments where a glass-ceramic consists of such oxides and embodiments where a glass-ceramic consists essentially of a such oxides.

It will be apparent to those skilled in the art that various modifications and variations can be made to the present invention without departing from the spirit and scope of the invention. Since modifications, combinations, sub-combinations and variations of the disclosed embodiments incorporating the spirit and substance of the invention may occur to persons skilled in the art, the invention should be construed to include everything within the scope of the appended claims and their equivalents. 

We claim:
 1. A glass-ceramic of the lithium aluminosilicate type, containing a β-quartz solid solution as the predominant crystalline phase and having for a thickness of 4 mm: an integrated optical transmission, T_(v), in the visible range, of 0.8 to 2%, an optical transmission at 625 nm of more than 3.5%, an optical transmission at 950 nm between 40 and 70%, and an optical transmission at 1,600 nm between 50 and 75%, wherein its composition, expressed as percentages by weight of oxides, comprises: SnO₂    0.2-<0.3; V₂O₅ 0.025-0.2; Cr₂O₃  0.01-0.04; Fe₂O₃ >0.095-0.32; As₂O₃ + Sb₂O₃ <0.1; and Fe₂O₃/V₂O₅ 1 to
 4.


2. The glass-ceramic according to claim 1, comprising SnO₂ 0.25-0.28.


3. The glass-ceramic according to claim 1, comprising Fe₂O₃ 0.12-0.29.


4. The glass-ceramic according to claim 1, comprising less than 200 ppm of CoO.
 5. The glass-ceramic according to claim 1, the composition of which is free of F and of Br, except for inevitable traces.
 6. The glass-ceramic according to claim 1, further comprising: SiO₂ 60-72 Al₂O₃ 18-23 Li₂O 2.5-4.5 MgO 0-3 ZnO 0-3 TiO₂ 1.5-4  ZrO₂  0-2.5 BaO 0-5 SrO 0-5 BaO + SrO 0-5 CaO 0-2 Na₂O  0-1.5 K₂O  0-1.5 P₂O₅   0-5, and B₂O₃  0-2.


7. The glass-ceramic according to claim 6, the composition of which comprises at least 98% by weight of SnO₂, V₂O₅, Cr₂O₃, Fe₂O₃, SiO₂, Al₂O₃, Li₂O, MgO, ZnO, TiO₂, ZrO₂, BaO, SrO, CaO, Na₂O, K₂O, P₂O₅ and B₂O₃.
 8. An article comprising the glass-ceramic according to claim
 1. 9. The article according to claim 8, selected from the group consisting of a cooktop, a cooking utensil and a microwave oven tray.
 10. A lithium aluminosilicate glass, having a composition expressed as percentages by weight of oxides, comprising: SnO₂    0.2-<0.3; V₂O₅ 0.025-0.2; Cr₂O₃  0.01-0.04; Fe₂O₃ >0.095-0.32; As₂O₃ + Sb₂O₃ <0.1; and Fe₂O₃/V₂O₅ 1 to
 4.


11. A method for forming an article according to claim 8, successively comprising: melting a load of vitrifiable raw materials, said load containing SnO₂ as a fining agent; fining of the obtained molten glass; cooling the fined molten glass and simultaneously shaping it to a desired shape for the article; and heat treating the shaped glass to transform the glass into a glass-ceramic. 